CN103025903B - Oriented electromagnetic steel plate and production method for same - Google Patents

Oriented electromagnetic steel plate and production method for same Download PDF

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Publication number
CN103025903B
CN103025903B CN201180036001.6A CN201180036001A CN103025903B CN 103025903 B CN103025903 B CN 103025903B CN 201180036001 A CN201180036001 A CN 201180036001A CN 103025903 B CN103025903 B CN 103025903B
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steel plate
annealing
magnetic domain
electron beam
magnetic
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CN103025903A (en
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大村健
山口广
冈部诚司
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JFE Steel Corp
JFE Engineering Corp
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NKK Corp
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    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
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    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
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    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation

Abstract

The present invention can obtain an oriented electromagnetic steel plate with magnetic domain refinement by electron beam irradiation and which achieves excellent low-noise characteristics when assembled on an existing transformer, as a result of: the ratio (Wa/Wb) between a film thickness (Wa) of a fosterite coating on a distortion introduction side of a steel plate and a film thickness (Wb) of the fosterite coating on a distortion non-introduction side being 0.5 or greater; the average width of a discontinuous section in a magnetic domain in the steel plate surface on the distortion introduction side being 150-300 [mu]m; and the average width of the discontinuous section in the magnetic domain in the steel plate surface on the distortion non-introduction side being 250-500 [mu]m.

Description

Grain-oriented magnetic steel sheet and manufacture method thereof
Technical field
The present invention relates to grain-oriented magnetic steel sheet and the manufacture method thereof of the core material being suitable as transformer etc.
Background technology
Grain-oriented magnetic steel sheet uses mainly as the iron core of transformer, and its magnetization characteristic of general requirement is excellent, particularly requires that iron loss is low.
Therefore, importantly make that the secondary recrystallization crystal grain in steel plate is highly consistent with (110) [001] orientation (so-called Gauss's orientation), the impurity reduced in finished steel plate.In addition, there is boundary with aspects such as the balances of manufacturing cost in the control of crystalline orientation, being reduced in of impurity.Therefore, developing and introducing ununiformity by physical method to surface of steel plate and make the width reduction of magnetic domain thus reduce technology, i.e. the magnetic domain refinement technology of iron loss.
Such as, in patent documentation 1, propose following technology: to final finished plate irradiating laser, to introducing high dislocation density areas, steel plate top layer, domain width is narrowed, reduce the iron loss of steel plate thus.The technology being controlled domain width by irradiating electron beam is proposed in patent documentation 2.
Prior art document
Patent documentation
Patent documentation 1: Japanese Patent Publication 57-2252 publication
Patent documentation 2: Japanese Patent Publication 06-072266 publication
Summary of the invention
Invent problem to be solved
But when being assembled in real transformer by the above-mentioned various grain-oriented magnetic steel sheets implementing magnetic domain thinning processing, the noise remaining real transformer becomes large problem.
The present invention develops in view of above-mentioned present situation just, therefore its object is to be provided in the grain-oriented magnetic steel sheet that can obtain excellent low noise and low iron loss characteristic when being assembled in real transformer, and provides its favourable manufacture method simultaneously.
For the method for dealing with problems
Contriver investigates the reason that the noise produced when the grain-oriented magnetic steel sheet after magnetic domain thinning processing is used for real transformer increases.Result is known, the reason that transformer noise increases is, at the forsterite tunicle in order to carry out strain introducing portion when thermal strain is introduced in magnetic domain refinement (with Mg 2siO 4tunicle for main body) thickness reduce.And distinguish with regard to this point, if the ratio that the thickness Wa strain of steel plate being introduced to the forsterite tunicle of side and unstrained introduce the thickness Wb of the forsterite tunicle of side suitably regulates, then noise can be prevented deteriorated.
In addition, the condition of the effect that can obtain the reduction iron loss brought by magnetic domain thinning processing is to greatest extent investigated, result is distinguished, needs the width average in the discontinuous portion of magnetic domain strain being introduced the width average in the discontinuous portion of magnetic domain of the surface of steel plate of side and the surface of steel plate of unstrained introducing side to be adjusted to suitable scope separately.At this, strain is introduced side and is referred to the side having irradiated electron beam, and unstrained is introduced side and referred to the side of not implementing electron beam irradiation.
The present invention is based on above-mentioned discovery and develop.
That is, described in purport of the present invention is constructed as follows.
1. a grain-oriented magnetic steel sheet, has forsterite tunicle on surface, utilize electron beam to implement strain and introduce and magneticflux-density B 8for more than 1.92T, wherein, the ratio (Wa/Wb) that thickness Wa and the unstrained of the forsterite tunicle of the strain introducing side of this steel plate introduce the thickness Wb of the forsterite tunicle of side is more than 0.5, and, the width average that the discontinuous portion of magnetic domain of the surface of steel plate of side is introduced in strain is 150 ~ 300 μm, and the width average that unstrained introduces the discontinuous portion of magnetic domain of the surface of steel plate of side is 250 ~ 500 μm.
2. the manufacture method of a grain-oriented magnetic steel sheet, directional electro-magnetic steel plate steel billet is rolled and after being refined to final thickness of slab, implement decarburizing annealing, then be coated with on surface of steel plate with MgO be main component annealing separation agent after carry out final annealing, then tensile coating is applied, and carry out the magnetic domain thinning processing utilizing electron beam irradiation after this final annealing or after applying this tensile coating, in described manufacture method
(1) vacuum tightness during electron beam irradiation is set as 0.1 ~ 5Pa,
(2) by smooth annealing time to steel plate give tension control be 5 ~ 15MPa.
3. the manufacture method of the grain-oriented magnetic steel sheet as described in above-mentioned 2, wherein, directional electro-magnetic steel plate steel billet carries out hot rolling, then implements hot-rolled sheet annealing as required, then implement once cold rolling or cold rolling across more than twice of process annealing, and be refined to final thickness of slab.
Invention effect
According to the present invention, can obtain in real transformer, also effectively can maintain the grain-oriented magnetic steel sheet by the effect of the reduction iron loss using the magnetic domain refinement of electron beam to bring, therefore, in real transformer, excellent low noise can be shown while the low iron loss of maintenance.
Accompanying drawing explanation
Fig. 1 represents for measuring forsterite by the figure in the cross section of film thickness.
Fig. 2 is the figure of the Domain Observation result representing steel plate.
Embodiment
Below, the present invention is specifically described.
In the present invention, for giving strain thus suppressing the main points of the noise increase of the real transformer of the grain-oriented magnetic steel sheet after using magnetic domain thinning processing to be all to meet following three main points.
(strain introduces the forsterite of side by the control of film thickness)
First main points are introduce to have the forsterite of the part of strain by the control of film thickness, and forsterite is as described below by the reason that the control of film thickness is important.
Steel plate tension force given by the forsterite tunicle of surface of steel plate.When the thickness of this forsterite tunicle changes, the tension distribution of steel plate becomes uneven.When tension distribution produces uneven, cause the magnetostrictive vibration wave shape of the steel plate of noise to deform, result, higher harmonic component is overlapping and cause noise to increase.Therefore, in order to suppress this noise to increase, importantly suppress the forsterite produced when introducing thermal strain by the minimizing of film thickness.That is, ratio (Wa/Wb) that the thickness Wa of the forsterite tunicle of side and unstrained introduce the thickness Wb of the forsterite tunicle of side is more than 0.5 to need to make strain to introduce.Be preferably more than 0.7.
It should be noted that, the thickness introducing the forsterite tunicle on the steel plate two sides before strain is generally equal extent.Therefore, the maximum value of Wa/Wb is about 1.
In addition, Fig. 1 is the schematic diagram in the steel plate cross section with forsterite tunicle.From short period, forsterite tunicle in uneven thickness and greatly concavo-convex, but by adopting enough mensuration distance, thickness can be determined according to its mean value.Specifically, cut the sample in steel plate cross section, predetermined mensuration distance (preferred 1mm) is obtained to the area (preferably using SEM to observe and image analysis) of forsterite tunicle, and calculate this face by the mean value of film thickness, the thickness of forsterite tunicle can be obtained thus.
Above-mentioned than (Wa/Wb) in order to meet, as previously mentioned, importantly suppress the forsterite implementing the part that thermal strain is given by the minimizing of film thickness, it suppresses means as described below.
First, good forsterite tunicle is importantly formed.At this, good forsterite tunicle refers to that the space caused by crackle etc. in tunicle is few and the forsterite tunicle that density is high.In addition, forsterite tunicle is caused have the greatest impact in the factor of crackle equivalent damage be in smooth annealing steel plate give tension force, when this tension force is strong, forsterite tunicle is impaired and crack.Therefore, in the annealing furnace that steel billet temperature is high and strain sensitive is high, needing tension control is 15MPa (1.5kgf/mm 2) below.
On the other hand, in the present invention, need to make mentioned strain be 5MPa (0.5kgf/mm 2) more than.This is because during lower than 5MPa, the shape correction of steel plate becomes insufficient.In addition, vacuum tightness when controlling electron beam irradiation is needed.When it is generally acknowledged electron beam irradiation, vacuum tightness is more high better.But the present inventor finds, in order to suppress the minimizing of forsterite tunicle, in electron beam irradiation, make oxygen moderately residual is effective.Its reason is not yet clear and definite, but thinks that steel plate is oxidized due to the oxygen remained when introducing thermal strain, and this serve impact may to the maintenance band of forsterite tunicle thickness.At this, in order to suppress the minimizing of forsterite tunicle thickness, need to make vacuum tightness to be the scope of 0.1 ~ 5Pa.When vacuum tightness is higher than 0.1Pa, the minimizing of forsterite tunicle cannot be suppressed.On the other hand, low vacuum, when 5Pa, cannot give thermal strain to steel plate effectively.Be more preferably the scope of 0.5 ~ 3Pa.
(control in the discontinuous portion of magnetic domain of the surface of steel plate of side and the surface of steel plate of unstrained introducing side is introduced in strain)
Second main points are the control that the discontinuous portion of magnetic domain of the surface of steel plate of side and the surface of steel plate of unstrained introducing side is introduced in strain.
By controlling the thickness of above-mentioned forsterite tunicle, can noise be suppressed to a certain extent to increase, but real transformer require low noise and low iron loss further.
That is, in order to reduce transformer iron loss, it is also important for reducing raw-material iron loss.That is, in order to fully obtain raw-material magnetic domain thinning effect, importantly:
I () introduces strain until also produce the discontinuous portion of magnetic domain at the surface of steel plate straining surface of steel plate and the unstrained introducing side of introducing side;
(ii) strain the deterioration that introducing can cause magnetic hysteresis loss, therefore, the narrowed width in the discontinuous portion of magnetic domain will be made as far as possible.
Meet above-mentioned (i) and (ii) every actual conditions and be that the width average making strain introduce the discontinuous portion of magnetic domain of the surface of steel plate of side is 150 ~ 300 μm and the width average making unstrained introduce the discontinuous portion of magnetic domain of the surface of steel plate of side is 250 ~ 500 μm.That is, the present invention is met above-mentioned (i) by the width average in the discontinuous portion of magnetic domain of the surface of steel plate of regulation unstrained introducing side, and is met above-mentioned (ii) by the higher limit setting respective width average.In addition, the lower value setting respective width average is because cannot obtain magnetic domain thinning effect when width is narrower than this lower value.
In addition, during vacuum tightness when the maximum tension when not meeting the smooth annealing as above-mentioned first main points and electron beam irradiation, meeting above-mentioned heat affecting width when not making the thickness of forsterite tunicle reduce is very difficult.
At this, it should be noted that the width average in the importantly discontinuous portion of magnetic domain in the present invention, instead of average shot width.That is, this is because, when introducing heat in steel plate, heat is expanded on all directions such as thickness of slab direction, plate width direction, and the discontinuous portion of magnetic domain being therefore subject to this heat affecting usually exists and becomes the tendency wider than irradiating width.In addition, for identical reason, compared with the discontinuous portion of magnetic domain introducing side with strain, the width that unstrained introduces the discontinuous portion of magnetic domain of side is wider.
In the present invention, the width in the discontinuous portion of magnetic domain can obtain by the following method: use the bit method etc. of magnetic colloid to make domain structure visualization, thus the discontinuous portion (with reference to figure 2) of electron beam irradiation formation can be identified by, and then predetermined mensuration distance (preferred 20mm) is measured to the width in the discontinuous portion of magnetic domain and calculates its mean value.At this, Fig. 2 is the schematic diagram of the domain structure representing grain-oriented magnetic steel sheet after magnetic domain thinning processing, it illustrates there is main magnetic domain in the lateral direction and with main magnetic domain substantially vertically irradiating electron beam and the situation obtained on the above-below direction of paper central authorities.The discontinuous portion of magnetic domain refers to the region that the structure of main magnetic domain is mixed and disorderly due to electron beam irradiation, and it is substantially corresponding with the region being subject to heat affecting by electron beam irradiation.
(aggregation degree of starting material crystal grain on easy magnetizing axis is high)
3rd main points are that the aggregation degree of starting material crystal grain on easy magnetizing axis is high.
For transformer noise and magnetostriction vibration, the aggregation degree of starting material crystal grain on easy magnetizing axis is higher, and vibration amplitude is less.Therefore, in order to suppress noise, need to make also as the magneticflux-density B of the index of the aggregation degree on easy magnetizing axis 8for more than 1.92T.At this, magneticflux-density B 8during lower than 1.92T, produce in magnetic history for the large magnetostriction of the rotary motion of the magnetic domain parallel with excitation field, therefore make the noise of transformer increase.In addition, aggregation degree is higher, and magnetic domain thinning effect is also higher, therefore, from the viewpoint of reduction iron loss, also needs to make magneticflux-density B 8for more than 1.92T.
Introduce process as strain of the present invention, be defined as can alleviate strain introducing portion by the method for the use electron beam of membrane damage.At this, when implementing electron beam irradiation, making direction of illumination be the direction of crossing rolling direction, being preferably the direction of 60 ° ~ 90 ° with rolling direction, and making the irradiation of electron beam be spaced apart about 3mm ~ about 15mm.In addition, use the electron beam irradiation condition that acceleration voltage is 10 ~ 200kV, electric current is 0.1 ~ 100mA and use the beam diameter (diameter) of 0.01 ~ 0.5mm to implement with point-like or wire.Preferred beam diameter is 0.01 ~ 0.3mm.
Below, the manufacturing condition of grain-oriented magnetic steel sheet of the present invention is specifically described.
In the present invention, the composition of steel for directional electromagnetic steel plate base consists of the one-tenth that secondary recrystallization occurs and is grouped into.
In addition, when using inhibitor, such as, when using AlN system inhibitor, appropriate containing Al and N, in addition when using MnSMnSe system inhibitor, appropriate containing Mn and Se and/or S.Certainly, two kinds of inhibitor can also be combinationally used.In this case, the preferred content of Al, N, S and Se is respectively Al:0.01 ~ 0.065 quality %, N:0.005 ~ 0.012 quality %, S:0.005 ~ 0.03 quality %, Se:0.005 ~ 0.03 quality %.
In addition, the present invention also can be applicable to limit the content of Al, N, S, Se and not use the grain-oriented magnetic steel sheet of inhibitor.
In this case, Al, N, S and Se amount preferably suppresses respectively for below Al:100 quality ppm, N:50 below quality ppm, below S:50 quality ppm, Se:50 below quality ppm.
Below, the basal component of steel for directional electromagnetic steel plate base of the present invention and optional added ingredients are specifically described.
Below C:0.08 quality %
C adds for improving hot-rolled sheet tissue, but during more than 0.08 quality %, increases, therefore, be preferably set to below 0.08 quality % for burden C being reduced to below the 50 quality ppm not causing magnetic aging in manufacturing process.In addition, about lower limit, even also can not secondary recrystallization be carried out, therefore without the need to special setting containing the starting material of C.
Si:2.0 ~ 8.0 quality %
Si is for the resistance improving steel and improves the effective element of iron loss, and when content is more than 2.0 quality %, the effect reducing iron loss is good especially.On the other hand, when content is below 8.0 quality %, processibility excellent especially, magneticflux-density can be obtained.Therefore, Si amount is preferably set to the scope of 2.0 ~ 8.0 quality %.
Mn:0.005 ~ 1.0 quality %
Mn make hot workability good in be favourable element, but content lower than 0.005 quality % time, its additive effect is not enough.On the other hand, when content is below 1.0 quality %, the magneticflux-density of production board is good especially.Therefore, Mn amount is preferably set to the scope of 0.005 ~ 1.0 quality %.
Except above-mentioned basal component, can also suitably contain element as described below as the composition improving magnetic properties.
Be selected from least one in Ni:0.03 ~ 1.50 quality %, Sn:0.01 ~ 1.50 quality %, Sb:0.005 ~ 1.50 quality %, Cu:0.03 ~ 3.0 quality %, P:0.03 ~ 0.50 quality %, Mo:0.005 ~ 0.10 quality % and Cr:0.03 ~ 1.50 quality %
Ni improves the useful element of magnetic properties further for improving hot-rolled sheet tissue further.But when content is lower than 0.03 quality %, the effect improving magnetic properties is little, and on the other hand, when content is below 1.5 quality %, the stability of secondary recrystallization especially increases, thus makes magnetic properties improve further.Therefore, Ni amount is preferably set to the scope of 0.03 ~ 1.5 quality %.
In addition, Sn, Sb, Cu, P, Mo and Cr are for improving the useful element of magnetic properties separately, but all do not meet above-mentioned each composition lower in limited time, the effect improving magnetic properties is little, on the other hand, when content is below the upper limit amount of above-mentioned each composition, the prosperity of secondary recrystallization crystal grain is the best.Therefore, preferably separately to contain with above-mentioned scope.
In addition, the surplus beyond mentioned component is the inevitable impurity and Fe that are mixed in manufacturing process.
Then, the steel billet with mentioned component composition is conventionally heated rear for hot rolling, but, also directly can carry out hot rolling without heating after casting.When thin cast piece, can hot rolling be carried out, also can omit hot rolling and operation after directly carrying out.
In addition, hot-rolled sheet annealing is implemented as required.The main purpose of hot-rolled sheet annealing is, eliminates the band tissue that produces in hot rolling and makes primary recrystallization tissue carry out whole grain, thus in secondary recrystallization annealing, makes the further prosperity of Goss texture and improve magnetic properties.Now, in order to make Goss texture flourishing at production board camber, preferably the scope of 800 ~ 1100 DEG C is as hot-roll annealing temperature.When hot-roll annealing temperature is lower than 800 DEG C, the band tissue residue in hot rolling, is difficult to realize the primary recrystallization tissue after carrying out whole grain, thus cannot obtain the improvement of the secondary recrystallization expected.On the other hand, when hot-roll annealing temperature is more than 1100 DEG C, the particle diameter too coarsening after hot-rolled sheet annealing, is therefore difficult to realize the primary recrystallization tissue after carrying out whole grain.
After hot-rolled sheet annealing, preferably implement once cold rolling or cold rolling across more than twice of process annealing, be then refined to final thickness of slab.Then, carry out decarburizing annealing (doubling as recrystallization annealing), and be coated with annealing separation agent.After coating annealing separation agent, carry out final annealing with the object that is formed as of secondary recrystallization and forsterite tunicle.In addition, for annealing separation agent, in order to form forsterite, be preferably main component with MgO.At this, MgO is that main component refers in the scope of the formation not damaging the forsterite tunicle as the object of the invention, can improve composition containing the known annealing separation agent composition beyond MgO, characteristic.
After the final anneal, it is effective for carrying out smooth annealing to correct shape.In addition, in the present invention, before smooth annealing or after smooth annealing, on surface of steel plate, apply insulating coating.At this, this insulating coating refers to, can give the coating (hereinafter referred to as tensile coating) of tension force in the present invention in order to reduce iron loss to steel plate.In addition, as tensile coating, the ceramic coating etc. the inorganic system coating containing silicon-dioxide can enumerated, use physical vapor deposition, chemical vapor deposition method etc. to be formed.
In the present invention, for the grain-oriented magnetic steel sheet after above-mentioned final annealing or after applying tensile coating, in above-mentioned either phase to surface of steel plate irradiating electron beam, implement magnetic domain thinning processing thus, by controlling vacuum tightness during irradiating electron beam as previously mentioned, the thermal strain brought by electron beam irradiation can be given full play to and give effect, and the damage reducing tunicle can be done one's utmost.
In the present invention, except above-mentioned operation, manufacturing condition, the manufacture method of the grain-oriented magnetic steel sheet of the magnetic domain thinning processing of all right known use electron beam of application implementation.
Embodiment 1
Manufacture grouping by continuous casting to become containing C:0.08 quality %, Si:3.1 quality %, Mn:0.05 quality %, Ni:0.01 quality %, Al:230 quality ppm, N:90 quality ppm, Se:180 quality ppm, S:20 quality ppm and O:22 quality ppm and surplus is the steel billet of Fe and inevitable impurity, after being heated to 1400 DEG C, make by hot rolling the hot-rolled sheet that thickness of slab is 2.0mm, at 1100 DEG C, then implement the hot-rolled sheet annealing of 120 seconds.Then, by the cold rolling middle thickness of slab making 0.65mm, and at oxidisability PH 2o/PH 2=0.32, temperature: 1000 DEG C, time: implement process annealing under the condition of 60 seconds.Then, after the sub-scale by chlorohydric acid pickling removing surface, again implement cold rolling, make the cold-reduced sheet that thickness of slab is 0.23mm.
Then, implement at oxidisability PH 2o/PH 2=0.50, soaking temperature: the decarburizing annealing keeping 60 seconds under the condition of 830 DEG C, then, coating take MgO as the annealing separation agent of main component, implements the final annealing for the purpose of secondary recrystallization, the formation of forsterite tunicle and purifying under the condition of 1200 DEG C, 30 hours.Then, coating comprises the colloidal silica of 60% and the insulating coating of aluminum phosphate, and sinters at 800 DEG C.This coating applications process also doubles as smooth annealing.
Then, to one side implement and the vertical direction of rolling direction on irradiating width: 0.15mm, irradiate interval: the magnetic domain thinning processing of 5.0mm irradiating electron beam, obtains finished product and evaluate magnetic properties.Change primary recrystallization annealing temperature and obtain magneticflux-density B 8value is the material of 1.90 ~ 1.95T.In addition, for electron beam irradiation, also change electron beam current value and beam scan velocity and irradiate with various condition.Then, oblique angle shearing is carried out to each finished product, the three-phase transformer of assembling 500kVA, and under excited state, measure iron loss and noise with 50Hz, 1.7T.In this transformer, the design load of iron loss and noise is 55dB, 0.83W/kg.
The measurement result of above-mentioned iron loss and noise is shown in Table 1.
As the table shows, when using enforcement utilize the magnetic domain thinning processing of electron beam and meet the grain-oriented magnetic steel sheet of scope of the present invention, the noise of real transformer is low, and the deterioration of iron loss characteristic is also inhibited, and is all met the characteristic of design load.
On the other hand, magneticflux-density departs from the comparative example of No.11 and No.12 of the scope of the invention, does not all obtain low noise and low iron loss simultaneously.In addition, (Wa/Wb) lower than 0.5 No.1 ~ 3 and 10 comparative example in, all do not obtain low noise.In addition, strain introduce width average that side or unstrained introduce the discontinuous portion of magnetic domain of the surface of steel plate of side depart from the scope of the invention No.6,8, in the comparative example of 9, iron loss is all poor.

Claims (3)

1. a grain-oriented magnetic steel sheet, has forsterite tunicle on surface, utilize electron beam to implement strain and introduce and magneticflux-density B 8for more than 1.92T, wherein, the ratio (Wa/Wb) that thickness Wa and the unstrained of the forsterite tunicle of the strain introducing side of this steel plate introduce the thickness Wb of the forsterite tunicle of side is more than 0.5, and, the width average that the discontinuous portion of magnetic domain of the surface of steel plate of side is introduced in strain is 150 ~ 300 μm, and the width average that unstrained introduces the discontinuous portion of magnetic domain of the surface of steel plate of side is 250 ~ 500 μm.
2. the manufacture method of a grain-oriented magnetic steel sheet, directional electro-magnetic steel plate steel billet is rolled and after being refined to final thickness of slab, implement decarburizing annealing, then, surface of steel plate is coated with MgO be main component annealing separation agent after carry out final annealing, then apply tensile coating, and carry out the magnetic domain thinning processing utilizing electron beam irradiation after this final annealing or after applying this tensile coating, in described manufacture method
(1) vacuum tightness during electron beam irradiation is set as 0.1 ~ 5Pa,
(2) by smooth annealing time to steel plate give tension control be 5 ~ 15MPa.
3. the manufacture method of grain-oriented magnetic steel sheet as claimed in claim 2, wherein, directional electro-magnetic steel plate steel billet carries out hot rolling, then implements hot-rolled sheet annealing as required, then implement once cold rolling or cold rolling across more than twice of process annealing, and be refined to final thickness of slab.
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Families Citing this family (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2597190C1 (en) 2012-08-30 2016-09-10 ДжФЕ СТИЛ КОРПОРЕЙШН Sheet of electrotechnical textured steel for iron core and method of its manufacturing
JP5987610B2 (en) 2012-09-28 2016-09-07 Ｊｆｅスチール株式会社 Steel plate inspection apparatus, steel plate inspection method, and steel plate manufacturing method
JP6149370B2 (en) * 2012-09-28 2017-06-21 Ｊｆｅスチール株式会社 Magnetic domain discontinuity detection method
JP5561335B2 (en) * 2012-09-28 2014-07-30 Ｊｆｅスチール株式会社 Electron gun abnormality detection device and electron gun abnormality detection method
CN104736728B (en) 2012-10-30 2016-08-24 杰富意钢铁株式会社 The manufacture method of low iron loss orientation electromagnetic steel plate
RU2611457C2 (en) 2012-10-31 2017-02-22 ДжФЕ СТИЛ КОРПОРЕЙШН Texture sheet of electric steel and method of its production
JP5668795B2 (en) * 2013-06-19 2015-02-12 Ｊｆｅスチール株式会社 Oriented electrical steel sheet and transformer core using the same
MX2016009420A (en) * 2014-01-23 2016-09-16 Jfe Steel Corp Directional magnetic steel plate and production method therefor.
BR112017007867B1 (en) * 2014-10-23 2021-03-02 Jfe Steel Corporation electrical grain-oriented steel sheet and process to produce the same
JP6191789B2 (en) * 2015-02-05 2017-09-06 Ｊｆｅスチール株式会社 Directional electrical steel sheet, method for manufacturing the same, and method for predicting transformer noise characteristics
KR102062182B1 (en) * 2015-02-13 2020-01-03 제이에프이 스틸 가부시키가이샤 Grain-oriented electrical steel sheet and method for manufacturing same
WO2016139818A1 (en) * 2015-03-05 2016-09-09 Ｊｆｅスチール株式会社 Directional magnetic steel plate and method for producing same
JP6465054B2 (en) 2016-03-15 2019-02-06 Ｊｆｅスチール株式会社 Production method and production equipment row of grain-oriented electrical steel sheets
MX2019010134A (en) 2017-02-28 2019-10-07 Jfe Steel Corp Grain-oriented electrical steel sheet and production method therefor.
US11236427B2 (en) 2017-12-06 2022-02-01 Polyvision Corporation Systems and methods for in-line thermal flattening and enameling of steel sheets
CN111886662B (en) * 2018-03-30 2023-05-12 杰富意钢铁株式会社 Iron core for transformer
MX2020010226A (en) * 2018-03-30 2020-11-06 Jfe Steel Corp Iron core for transformer.
MX2021006700A (en) 2018-12-05 2021-07-07 Jfe Steel Corp Grain-oriented electromagnetic steel sheet and production method therefor.
BR112021010673A2 (en) * 2018-12-28 2021-08-24 Nippon Steel Corporation Grain-oriented electrical steel sheet and manufacturing method
KR102276850B1 (en) * 2019-12-19 2021-07-12 주식회사 포스코 Grain oriented electrical steel sheet and method for refining magnetic domains therein
EP4223891A4 (en) * 2020-11-27 2023-11-01 JFE Steel Corporation Grain-oriented electromagnetic steel sheet and method for manufacturing same

Family Cites Families (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5652117B2 (en) * 1973-11-17 1981-12-10
JPS5518566A (en) 1978-07-26 1980-02-08 Nippon Steel Corp Improving method for iron loss characteristic of directional electrical steel sheet
GR75219B (en) 1980-04-21 1984-07-13 Merck & Co Inc
US4909864A (en) * 1986-09-16 1990-03-20 Kawasaki Steel Corp. Method of producing extra-low iron loss grain oriented silicon steel sheets
JPH0672266B2 (en) 1987-01-28 1994-09-14 川崎製鉄株式会社 Method for manufacturing ultra low iron loss unidirectional silicon steel sheet
JPH0617513B2 (en) * 1986-11-13 1994-03-09 新日本製鐵株式会社 Method for flattening annealing of unidirectional silicon steel sheet with excellent magnetic properties and coating adhesion
JP2683071B2 (en) * 1988-12-15 1997-11-26 川崎製鉄株式会社 Annealing method for grain-oriented silicon steel sheet
JPH0483825A (en) 1990-07-27 1992-03-17 Kawasaki Steel Corp Flattening annealing method for grain-oriented silicon steel sheet
JPH0551645A (en) * 1991-08-20 1993-03-02 Kawasaki Steel Corp Manufacture of low core loss grain-oriented silicon steel sheet
JPH05209226A (en) 1992-01-29 1993-08-20 Kawasaki Steel Corp Method for continuously flatten-annealing grain oriented electrical steel sheet
JPH05295446A (en) * 1992-04-20 1993-11-09 Kawasaki Steel Corp Device for reducing iron loss for grain-oriented silicon steel sheet
JPH05311241A (en) * 1992-05-08 1993-11-22 Kawasaki Steel Corp Manufacture of low core loss grain-oriented silicon steel sheet and irradiation device for electron beam
JP3082460B2 (en) 1992-08-31 2000-08-28 タカタ株式会社 Airbag device
JP3399991B2 (en) 1992-10-23 2003-04-28 川崎製鉄株式会社 Method for producing low iron loss unidirectional silicon steel sheet
US5296051A (en) * 1993-02-11 1994-03-22 Kawasaki Steel Corporation Method of producing low iron loss grain-oriented silicon steel sheet having low-noise and superior shape characteristics
JPH11158556A (en) 1997-11-28 1999-06-15 Nippon Steel Corp Production of grain-oriented silicon steel sheet
KR100359622B1 (en) * 1999-05-31 2002-11-07 신닛뽄세이테쯔 카부시키카이샤 High flux density grain-oriented electrical steel sheet excellent in high magnetic field core loss property and method of producing the same
JP2002220642A (en) * 2001-01-29 2002-08-09 Kawasaki Steel Corp Grain-oriented electromagnetic steel sheet with low iron loss and manufacturing method therefor
DE10130308B4 (en) * 2001-06-22 2005-05-12 Thyssenkrupp Electrical Steel Ebg Gmbh Grain-oriented electrical sheet with an electrically insulating coating
JP5181571B2 (en) * 2007-08-09 2013-04-10 Ｊｆｅスチール株式会社 Chromium-free insulating coating solution for grain-oriented electrical steel sheet and method for producing grain-oriented electrical steel sheet with insulation film
JP5262228B2 (en) * 2008-03-26 2013-08-14 Ｊｆｅスチール株式会社 Oriented electrical steel sheet and manufacturing method thereof
JP5927754B2 (en) * 2010-06-29 2016-06-01 Ｊｆｅスチール株式会社 Oriented electrical steel sheet and manufacturing method thereof

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